EP0237721B1 - Aluminiumberuhigter Vergütungsstahl - Google Patents

Aluminiumberuhigter Vergütungsstahl Download PDF

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Publication number
EP0237721B1
EP0237721B1 EP87100763A EP87100763A EP0237721B1 EP 0237721 B1 EP0237721 B1 EP 0237721B1 EP 87100763 A EP87100763 A EP 87100763A EP 87100763 A EP87100763 A EP 87100763A EP 0237721 B1 EP0237721 B1 EP 0237721B1
Authority
EP
European Patent Office
Prior art keywords
zirconium
aluminium
treatable steel
steel
heat
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP87100763A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP0237721A2 (de
EP0237721A3 (en
Inventor
Cestmir Dr.-Ing. Lang
Lutz Dr.-Ing. Meyer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Thyssen Stahl AG
Original Assignee
Thyssen Stahl AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=6294145&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP0237721(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Thyssen Stahl AG filed Critical Thyssen Stahl AG
Priority to AT87100763T priority Critical patent/ATE59065T1/de
Publication of EP0237721A2 publication Critical patent/EP0237721A2/de
Publication of EP0237721A3 publication Critical patent/EP0237721A3/de
Application granted granted Critical
Publication of EP0237721B1 publication Critical patent/EP0237721B1/de
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Definitions

  • the invention relates to an aluminum-hardened tempering steel with good hardenability.
  • the hardening depth is a measure of the hardenability of steels. It is usually defined as the distance from the surface at which 50% of the structure still consists of martensite.
  • unalloyed and alloyed tempering steels require a coarse austenite grain (ASTM grain number 6 or less) when austenitizing before hardening.
  • the coarse austenite grain has hitherto been limited to a max. 0.005% with usual and to max. 0.010% reached at elevated austenitizing temperatures.
  • Tempering steels with good hardenability have not hitherto been able to be produced by continuous casting because, for reasons of castability and product properties, minimum aluminum contents of the order of more than 0.010% are prescribed in the production of continuous castings. This is particularly disadvantageous because of the increased use of the economical continuous casting process in the steel industry.
  • austenitizing temperatures in the range between 950 and 1050 ° C would be required to achieve a coarse-grained austenite. Austenitizing temperatures of this kind are unacceptable, both for reasons of energy costs and due to technical limitations and scaling.
  • the hardenability loss of tempered tempered steels can be compensated for by adding alloying elements such as manganese or chromium.
  • alloying elements such as manganese or chromium.
  • these measures can only be carried out with restrictions.
  • the individual steel grades are to be delivered according to certain analysis instructions. Deviations from these regulations will not be tolerated.
  • the invention has for its object to reduce the adverse influence of aluminum on the hardenability of aluminum-hardened tempering steels with justifiable and economical means and to propose an aluminum-hardened hardening steel with improved hardenability, which can be inexpensively produced by the continuous casting process.
  • the addition of the nitrogen-affine element zirconium prevents the aluminum nitride precipitation in the steel, which would lead to a fine austenite grain.
  • zirconium By adding zirconium, however, coarse nitrides are formed when the steel solidifies.
  • a coarse austenite grain ASTM: 2 to 6
  • ASTM Standard austenitizing temperatures of approximately 800 to 860 ° C. and holding times over 10 minutes, corresponds to that of a silicon-calmed steel.
  • a zirconium additive leads to excellent hardenability regardless of the carbon content.
  • the carbon content is preferably 0.41 to 1.0%, the manganese content 0.20 to 2.0%, the silicon content to 0.5%, the nitrogen content 0.002 to 0.0065% Aluminum content 0.015 to 0.08% and the zirconium content 0.015 to 0.065%. But even with even lower manganese contents of 0.20 to 1.2% or 0.40 to 1.0%, the hardened steel has excellent hardenability.
  • the tempering steel according to the invention can also add chromium, nickel, molybdenum individually or to contain several, namely 0.05 to 3.5%, in particular 0.05 to 1.5% chromium and / or nickel and / or 0.05 to 0.5% molybdenum.
  • the steel In order not to impair the good hardenability of the steel according to the invention, however, the steel must not contain any alloying elements, such as niobium or titanium, which would lead to a fine grain in the austenite and, moreover, via germs in the structure, the austenite conversion in the ferrite / pearlite stage in the would accelerate hardening.
  • alloying elements such as niobium or titanium
  • the particular advantage of the heat-treatable steel according to the invention can be seen in the fact that the hardenability is adjusted to the level of the silicon-stabilized steels without a significant change in the analysis specification and without impairing the mechanical properties, and the use of the economical continuous casting process is made possible.
  • Another advantage of the aluminum calming and addition of zirconium in the tempering steel according to the invention is the assurance of aging resistance. Conventional tempering steels have free nitrogen and are therefore susceptible to aging.
  • the steel is preferably produced by continuous casting.
  • Steels A to M were melted in an oxygen inflation process.
  • the chemical composition and austenite grain size, determined as quenching grain size according to DIN 50601, of the steels are shown in Table 1.
  • Steels A to H fall under the invention.
  • Steels I and J, which have no addition of zirconium, and steels K and L, which have an Al content below 0.010%, and steel M, which shows a Zr / N ratio of less than 7, are not included The invention.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Articles (AREA)
  • Lubricants (AREA)
  • Heat Treatment Of Steel (AREA)
  • Laminated Bodies (AREA)
  • Forms Removed On Construction Sites Or Auxiliary Members Thereof (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Continuous Casting (AREA)
EP87100763A 1986-02-15 1987-01-21 Aluminiumberuhigter Vergütungsstahl Expired - Lifetime EP0237721B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT87100763T ATE59065T1 (de) 1986-02-15 1987-01-21 Aluminiumberuhigter verguetungsstahl.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE3604789 1986-02-15
DE3604789A DE3604789C1 (de) 1986-02-15 1986-02-15 Verguetungsstahl

Publications (3)

Publication Number Publication Date
EP0237721A2 EP0237721A2 (de) 1987-09-23
EP0237721A3 EP0237721A3 (en) 1988-04-20
EP0237721B1 true EP0237721B1 (de) 1990-12-12

Family

ID=6294145

Family Applications (1)

Application Number Title Priority Date Filing Date
EP87100763A Expired - Lifetime EP0237721B1 (de) 1986-02-15 1987-01-21 Aluminiumberuhigter Vergütungsstahl

Country Status (11)

Country Link
US (1) US4741880A (forum.php)
EP (1) EP0237721B1 (forum.php)
JP (1) JPS62253756A (forum.php)
KR (1) KR930006298B1 (forum.php)
CN (1) CN1011794B (forum.php)
AT (1) ATE59065T1 (forum.php)
AU (1) AU585694B2 (forum.php)
CA (1) CA1282982C (forum.php)
DE (2) DE3604789C1 (forum.php)
ES (1) ES2020201B3 (forum.php)
IN (1) IN167262B (forum.php)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4820486A (en) * 1985-04-05 1989-04-11 Kabushiki Kaisha Kobe Seiko Sho Low alloy steel having good stress corrosion cracking resistance
US5133928A (en) * 1989-10-28 1992-07-28 Chesterfield Cylinders Limited Cylinder body of a steel composition
US5185162A (en) * 1991-06-17 1993-02-09 Xaloy, Incorporated Corrosion and wear resistant bimetallic cylinder
JP2008514872A (ja) * 2004-09-28 2008-05-08 ガル ウント ザイツ ゲゼルシャフト ミット ベシュレンクテル ハフツング 二重壁管
CN1296509C (zh) * 2005-03-10 2007-01-24 武汉钢铁(集团)公司 高强度易焊接时效硬化钢及其生产方法
DE102013004905A1 (de) 2012-03-23 2013-09-26 Salzgitter Flachstahl Gmbh Zunderarmer Vergütungsstahl und Verfahren zur Herstellung eines zunderarmen Bauteils aus diesem Stahl
CN103397269A (zh) * 2013-07-01 2013-11-20 安徽三联泵业股份有限公司 低成本高强度耐磨铸钢及其制备方法
KR101986187B1 (ko) * 2017-11-08 2019-06-05 한국기계연구원 주조강
JP2021511992A (ja) 2017-11-16 2021-05-13 フィロ、アンドレ カンディド 複合材料、その製造方法、複合材料の使用方法及び複合材料を含む製品
CN112159928B (zh) * 2020-09-28 2021-11-12 广东韶钢松山股份有限公司 一种含Zr轴承钢及其制备方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3259488A (en) * 1960-03-31 1966-07-05 Ishikawajima Harima Heavy Ind Nitride-bearing low carbon ductile steels
GB1342582A (en) * 1970-03-20 1974-01-03 British Steel Corp Rail steel
FR2178319A5 (fr) * 1972-03-28 1973-11-09 Ugine Aciers Nouvelles applications d'aciers a haute frequence
JPS544321B2 (forum.php) * 1973-02-16 1979-03-06
JPS51132109A (en) * 1975-05-14 1976-11-17 Kobe Steel Ltd Grain-size conditioning free cutting steel
SU810832A1 (ru) * 1979-03-07 1981-03-07 Предприятие П/Я М-5481 Способ выплавки азотосодержащейбыСТРОРЕжущЕй СТАли
AU8261182A (en) * 1981-04-22 1982-10-28 Unisearch Limited Oxidation and corrosion-resistant febase-al-mn alloys
AU535458B2 (en) * 1982-02-22 1984-03-22 Kubota Ltd. Heat resisting alloy for rolls
JPS58221259A (ja) * 1982-06-18 1983-12-22 Daido Steel Co Ltd 機械構造用鋼
JPH05212611A (ja) * 1992-01-31 1993-08-24 Shinkusu Kk 溶接角柱のデポ処理兼用開先加工装置

Also Published As

Publication number Publication date
IN167262B (forum.php) 1990-09-29
AU6871187A (en) 1987-08-20
KR930006298B1 (ko) 1993-07-12
CN87102168A (zh) 1987-09-16
DE3766633D1 (de) 1991-01-24
US4741880A (en) 1988-05-03
CA1282982C (en) 1991-04-16
ATE59065T1 (de) 1990-12-15
ES2020201B3 (es) 1991-08-01
KR870008046A (ko) 1987-09-23
DE3604789C1 (de) 1987-08-20
JPS62253756A (ja) 1987-11-05
EP0237721A2 (de) 1987-09-23
EP0237721A3 (en) 1988-04-20
CN1011794B (zh) 1991-02-27
AU585694B2 (en) 1989-06-22

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